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Article(id=1241406713329415147, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1241406711219680205, articleNumber=null, orderNo=null, doi=10.3969/j.issn.0253-6099.2024.06.030, pmid=null, cstr=null, oa=null, hot=null, price=null, onlineType=0, articleFormat=0, articleType=null, articleTypeStr=null, receivedDate=1719244800000, receivedDateStr=2024-06-25, revisedDate=null, revisedDateStr=null, acceptedDate=null, acceptedDateStr=null, onlineDate=1773904024678, onlineDateStr=2026-03-19, pubDate=1732982400000, pubDateStr=2024-12-01, doiRegisterDate=null, doiRegisterDateStr=null, onlineIssueDate=1773904024678, onlineIssueDateStr=2026-03-19, onlineJustAcceptDate=null, onlineJustAcceptDateStr=null, onlineFirstDate=null, onlineFirstDateStr=null, sourceXml=null, magXml=null, createTime=1773904024678, creator=13701087609, updateTime=1773904024678, updator=13701087609, issue=Issue{id=1241406711219680205, tenantId=1146029695717560320, journalId=1235980550691926019, year='2024', volume='44', issue='6', pageStart='1', pageEnd='174', issueExtLink='null', onlineDate='null', pubDate='null', beforeIssueId=null, nextIssueId=null, price=null, status=1, issueComplete=1, articleOrder=1, issueType=-1, specialIssue=null, createTime=1773904024176, creator=13701087609, updateTime=1773911273793, updator=13701087609, preIssue=null, nextIssue=null, ext={EN=IssueExt(id=1241437118384362345, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1241406711219680205, language=EN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=), CN=IssueExt(id=1241437118388556650, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1241406711219680205, language=CN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=)}, issueFiles=null}, startPage=139, endPage=143, ext={EN=ArticleExt(id=1241406713597850612, articleId=1241406713329415147, tenantId=1146029695717560320, journalId=1235980550691926019, language=EN, title=Effect of Ultrasonic Melt Treatment on Microstructure and Hardening of Al-Cu-Mg-Ag Alloys, columnId=1236276108207902848, journalTitle=Mining and Metallurgical Engineering, columnName=MATERIALS, runingTitle=null, highlight=null, articleAbstract=

Al-Cu-Mg-Ag alloy melt was treated with ultrasonic waves, and the effect of the ultrasonic melt treatment on the microstructure and hardness of alloy was investigated. The results show that compared to the as-cast alloy without ultrasonic treatment, the as-cast alloy after ultrasonic melt treatment for 90 s and 180 s respectively has its hardness correspondingly improved by 12.7% and 11.2%. The ultrasonic melt treatment can reduce the segregation of alloy composition and accelerate precipitation of Ω phase during 2 h aging process at 200 ℃. A quantitative analysis shows that ultrasonic melt treatment can reduce the grain size of as-cast alloy, but presents limited effect of fine grain strengthening. Solid solution strengthening and precipitation strengthening respectively improve the hardness of as-cast and T6-tempered alloys.

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利用超声波处理Al-Cu-Mg-Ag合金熔体，研究了熔体超声处理对其微观组织和硬度的影响。结果表明，相较于未超声处理的铸态合金，熔体超声处理90 s和180 s所得铸态合金硬度分别提升了12.7%和11.2%。熔体超声处理降低了合金成分偏析，加快200 ℃/2 h时效过程中Ω相的析出。定量分析结果表明：熔体超声处理虽然能减小铸态合金的晶粒尺寸，但细晶强化效果有限；固溶强化和析出强化分别提高了铸态和T6态合金的硬度。

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柏松（1984—），男，江苏盐城人，副教授，主要从事铝合金组织调控与强韧化研究。E-mail：
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毛盼（1999—），女，湖南娄底人，硕士，主要从事铝合金热处理工艺研究。E-mail：

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毛盼（1999—），女，湖南娄底人，硕士，主要从事铝合金热处理工艺研究。E-mail：

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毛盼（1999—），女，湖南娄底人，硕士，主要从事铝合金热处理工艺研究。E-mail：

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journalId=1235980550691926019, articleId=1241406713329415147, doi=null, pmid=null, pmcid=null, year=2020, volume=139, issue=6, pageStart=3427, pageEnd=3440, url=null, language=null, rfNumber=[1], rfOrder=0, authorNames=ZAMANI M, TOSCHI S, MORRI A, journalName=Journal of Thermal Analysis and Calorimetry, refType=null, unstructuredReference=ZAMANI M, TOSCHI S, MORRI A, et al. 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（a）UT-0；（b）UT-90；（c）UT-180

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（a）UT-0；（b）UT-90；（c）UT-180

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（a）UT-0；（b）UT-90；（c）UT-180

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（a）UT-0；（b）UT-90；（c）UT-180

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合金编号CuMgAgTiFeSiAl
UT-04.930.631.020.020.030.03余量
UT-904.910.641.030.020.020.02余量
UT-1804.870.661.010.030.020.03余量
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实验合金化学成分（质量分数）

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合金编号CuMgAgTiFeSiAl
UT-04.930.631.020.020.030.03余量
UT-904.910.641.030.020.020.02余量
UT-1804.870.661.010.030.020.03余量
), ArticleFig(id=1241406722779181486, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=EN, label=null, caption=null, figureFileSmall=null, figureFileBig=null, tableContent=
合金编号铸态T6态
UT-094.6±4.0157.2±4.1
UT-90106.6±6.4166.9±3.4
UT-180105.2±6.0165.9±5.5
), ArticleFig(id=1241406722875650483, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=CN, label=表2, caption=

不同铸态及T6态合金的维氏硬度值（HV）

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合金编号铸态T6态
UT-094.6±4.0157.2±4.1
UT-90106.6±6.4166.9±3.4
UT-180105.2±6.0165.9±5.5
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位置AlCuMgAgTiFeSi
164.3519.1311.144.570.160.490.17
281.1813.144.160.880.090.340.20
368.1329.041.750.670.170.23—
467.6322.965.652.970.150.530.11
570.7023.853.781.190.190.29—
668.5822.786.182.460.060.330.21
), ArticleFig(id=1241406723068588484, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=CN, label=表3, caption=

不同位置能谱分析结果（原子分数）

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位置AlCuMgAgTiFeSi
164.3519.1311.144.570.160.490.17
281.1813.144.160.880.090.340.20
368.1329.041.750.670.170.23—
467.6322.965.652.970.150.530.11
570.7023.853.781.190.190.29—
668.5822.786.182.460.060.330.21
), ArticleFig(id=1241406723207000524, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=EN, label=null, caption=null, figureFileSmall=null, figureFileBig=null, tableContent=
位置AlCuMgAgTiFeSi
797.451.500.340.660.02—0.03
897.071.700.390.760.08——
996.961.910.340.750.03—0.01
), ArticleFig(id=1241406724767281626, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=CN, label=表4, caption=

高倍像区域内基体的能谱分析结果（质量分数）

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位置AlCuMgAgTiFeSi
797.451.500.340.660.02—0.03
897.071.700.390.760.08——
996.961.910.340.750.03—0.01
), ArticleFig(id=1241406725031522783, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=EN, label=null, caption=null, figureFileSmall=null, figureFileBig=null, tableContent=
合金编号平均晶粒尺寸/μm晶界占比/%
小角度晶界（2°～10°）大角度晶界（>10°）
UT-0154.4±86.212.187.9
UT-90149.0±86.611.089.0
UT-180145.4±76.315.284.8
), ArticleFig(id=1241406725174129134, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=CN, label=表5, caption=

铸态合金的EBSD分析结果

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合金编号平均晶粒尺寸/μm晶界占比/%
小角度晶界（2°～10°）大角度晶界（>10°）
UT-0154.4±86.212.187.9
UT-90149.0±86.611.089.0
UT-180145.4±76.315.284.8
), ArticleFig(id=1241406725283181046, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=EN, label=null, caption=null, figureFileSmall=null, figureFileBig=null, tableContent=
合金编号平均直径/nm平均厚度/nm数量密度/μm-3
UT-035.3±4.01.8±0.1576.9±69.2
UT-9033.3±2.01.4±0.2820.2±51.1
UT-18034.1±5.71.5±0.1826.7±75.9
), ArticleFig(id=1241406725396427262, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1241406713329415147, language=CN, label=表6, caption=

T6态合金组织Ω相的平均尺寸和数量密度

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合金编号平均直径/nm平均厚度/nm数量密度/μm-3
UT-035.3±4.01.8±0.1576.9±69.2
UT-9033.3±2.01.4±0.2820.2±51.1
UT-18034.1±5.71.5±0.1826.7±75.9
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熔体超声处理对Al-Cu-Mg-Ag合金微观组织和硬度的影响
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毛盼 , 王吉祥 , 柏松 , 刘志义
矿冶工程杂志 | 材料 2024,44(6): 139-143
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矿冶工程杂志 | 材料 2024, 44(6): 139-143
熔体超声处理对Al-Cu-Mg-Ag合金微观组织和硬度的影响
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毛盼 , 王吉祥, 柏松 , 刘志义
作者信息
  • 中南大学　材料科学与工程学院，湖南　长沙　410083

    • 毛盼（1999—），女，湖南娄底人，硕士，主要从事铝合金热处理工艺研究。E-mail：

通讯作者:

柏松（1984—），男，江苏盐城人，副教授，主要从事铝合金组织调控与强韧化研究。E-mail：
Effect of Ultrasonic Melt Treatment on Microstructure and Hardening of Al-Cu-Mg-Ag Alloys
Pan MAO , Jixiang WANG, Song BAI , Zhiyi LIU
Affiliations
  • School of Material Science and Engineering, Central South University, Changsha 410083, Hunan, China
出版时间: 2024-12-01 doi: 10.3969/j.issn.0253-6099.2024.06.030
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摘要
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利用超声波处理Al-Cu-Mg-Ag合金熔体，研究了熔体超声处理对其微观组织和硬度的影响。结果表明，相较于未超声处理的铸态合金，熔体超声处理90 s和180 s所得铸态合金硬度分别提升了12.7%和11.2%。熔体超声处理降低了合金成分偏析，加快200 ℃/2 h时效过程中Ω相的析出。定量分析结果表明：熔体超声处理虽然能减小铸态合金的晶粒尺寸，但细晶强化效果有限；固溶强化和析出强化分别提高了铸态和T6态合金的硬度。

Al-Cu-Mg-Ag合金  /  超声处理  /  硬度  /  微观组织  /  固溶强化  /  析出强化  /  T6热处理

Al-Cu-Mg-Ag alloy melt was treated with ultrasonic waves, and the effect of the ultrasonic melt treatment on the microstructure and hardness of alloy was investigated. The results show that compared to the as-cast alloy without ultrasonic treatment, the as-cast alloy after ultrasonic melt treatment for 90 s and 180 s respectively has its hardness correspondingly improved by 12.7% and 11.2%. The ultrasonic melt treatment can reduce the segregation of alloy composition and accelerate precipitation of Ω phase during 2 h aging process at 200 ℃. A quantitative analysis shows that ultrasonic melt treatment can reduce the grain size of as-cast alloy, but presents limited effect of fine grain strengthening. Solid solution strengthening and precipitation strengthening respectively improve the hardness of as-cast and T6-tempered alloys.

Al-Cu-Mg-Ag alloy  /  ultrasonic treatment  /  hardness  /  microstructure  /  solid solution strengthening  /  precipitation strengthening  /  T6 heat treatment
毛盼, 王吉祥, 柏松, 刘志义. 熔体超声处理对Al-Cu-Mg-Ag合金微观组织和硬度的影响. 矿冶工程杂志, 2024 , 44 (6) : 139 -143 . DOI: 10.3969/j.issn.0253-6099.2024.06.030
Pan MAO, Jixiang WANG, Song BAI, Zhiyi LIU. Effect of Ultrasonic Melt Treatment on Microstructure and Hardening of Al-Cu-Mg-Ag Alloys[J]. Mining and Metallurgical Engineering, 2024 , 44 (6) : 139 -143 . DOI: 10.3969/j.issn.0253-6099.2024.06.030
正文
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Al-Cu-Mg-Ag合金因其卓越的力学性能和热稳定性，在航空航天领域极具应用前景[1-3]。该合金时效后在｛111｝α面上形成均匀分布的细小Ω相，该相具有较高的沉淀硬化能力和良好的抗粗化能力[4-5]，赋予合金优异的高温力学性能。目前，铸造仍是不少铝合金构件的重要制备方法，但铸造产品往往伴随着各种缺陷，如枝晶偏析、孔洞和成分不均匀等，这些缺陷严重降低铸件质量。有研究表明，在铸造过程中引入超声波，通过超声效应改变合金熔体中溶质的扩散行为和温度分布，能达到减少铸造合金缺陷和改善合金性能的效果[6-7]。但目前熔体超声处理的研究主要集中于Al-Si系合金、镁合金和部分Al-Cu系合金的晶粒细化方面[7-10]，而熔体超声处理Al-Cu-Mg-Ag合金的相关研究很少。本文探究熔体超声处理对Al-Cu-Mg-Ag合金组织和性能的影响。
1　实验材料与方法
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实验所用合金通过工业纯铝及其他中间合金熔炼铸造而成，使用六氯乙烷（C2Cl6）对熔体进行除气处理，静置10 min后，在浇铸前对熔体进行超声处理（UT），功率为2 kW，将超声处理90 s和180 s的合金分别编号为UT-90和UT-180，未进行超声处理的合金编号为UT-0，各合金化学成分如表1所示。铸态合金的T6热处理工艺为：515 ℃/3 h固溶+水淬+200 ℃/2 h时效。采用小负荷维氏硬度机测试试样维氏硬度，载荷5 kg，加载时间15 s，每个状态取3个样品，每个样品测试4个点，结果取平均值。利用配备EDAX Genesis-2000型能谱仪的FEI Quanta-200环境扫描电镜（SEM）对合金第二粒子的形态和分布进行研究，操作电压20 kV。在Tescan Mira 4型SEM上进行电子背散射衍射（EBSD），使用AZtec Crystal 2.1软件对EBSD数据进行分析，EBSD样品首先用150#～2000#砂纸机械研磨后，再在10%HClO4+90%CH3CH2OH溶液中电解抛光。在Tecnai G220透射电镜（TEM）上观察T6态合金的组织，工作电压为200 kV。TEM样品机械研磨至80～100 μm后，冲取直径3 mm的圆片，并使用25%HNO3+75% CH3OH混合溶液进行双喷电解抛光。所有TEM定量分析均在近<110>α带轴所拍摄的图像上进行。
2　实验结果
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2.1　铸态合金硬度
表2为不同铸态及T6态合金的维氏硬度。从表2可看出，超声处理后的铸态合金及T6态合金的硬度值均明显高于相应的未经超声处理的合金。相比于铸态UT-0合金，铸态UT-90和UT-180合金硬度分别提升了12.7%和11.2%，即超声处理可以提升铸态合金的硬度。
2.2　铸态合金的微观组织
图1为铸态合金的背散射电子（BSE）图像。从图1可看出，铸态UT-0合金中存在明显的呈连续网状分布的枝晶偏析。经过超声处理后，UT-90和UT-180合金的枝晶偏析明显减少且呈间断分布，同时超声处理的合金内部出现了许多细小的球形或椭圆形共晶相。基于对多张铸态合金BSE图像的定量统计发现，UT-0合金的残余第二相面积分数为5.5%±0.8%，UT-90和UT-180合金的残余第二相面积分数分别为3.7%±0.6%和3.8%±0.4%，即超声处理能显著降低铸态合金的未溶相含量。对图1中标记处进行能谱分析，结果如表3～4所示。从表3可知，位置3处Cu原子分数高，且Al/Cu原子比接近2∶1，可认为该相为Al2Cu相。而晶内（位置1、2、4和5）主要存在Cu原子分数高和Mg、Ag原子分数低的共晶相。在枝晶偏析处也可以观察到这种共晶相（位置6）。同时表4中3种铸态合金基体的能谱分析结果显示，超声处理合金基体内Cu、Ag元素质量分数要高于未超声处理合金，Mg元素质量分数基本相当。
图2为3种铸态合金晶粒组织的反极图。从图2可以看出，3种合金中没有明显的晶粒择优取向。3种合金的EBSD分析结果见表5。从表5可知，铸态合金的平均晶粒尺寸随着超声时间延长逐渐减小，但3种合金大小、角度晶界占比差异不大。可见，熔体超声处理能在一定程度上细化铸态晶粒，但对大、小角度晶界占比的影响不明显。
2.3　T6态合金的微观组织
图3为3种铸态合金经T6处理后（T6态）组织的BSE图像。与图1相比，T6态合金的第二相数量明显减少，即固溶处理后发生明显回溶。图3中3种合金的第二相衬度均为浅灰色，结合铸态合金微观组织观察结果可知，该残余相为Al2Cu相，同时未发现类似图1中的球形共晶相。定量分析结果表明，T6态合金残余第二相面积分数从UT-0合金的1.3%±0.1%分别降至UT-90合金的1.0%±0.1%和UT-180合金的1.0%±0.2%。
T6态合金组织的TEM表征及定量分析结果见图4、图5和表6。从图4可以看出，T6态合金微观组织中的强化相均以Ω相为主，这与相应选区电子衍射花样上1/3和2/3｛220｝α位置处强烈的Ω相衍射斑点相吻合。在衍射花样的1/2｛220｝α位置未发现明显由θ′相产生的衍射，表明T6态合金中θ′相数量非常少。由图5发现，3种T6态合金组织中Ω相的分布规律较为相似，均主要集中在直径10～30 nm范围内。从表6可见，3种合金的Ω相平均直径没有明显差异，但超声处理后，Ω相的平均厚度降低且数量密度明显增加。
3　讨论
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3.1　超声处理对Ω相演变的影响
由图4、图5和表6可知，经过T6处理后，超声处理合金的Ω相平均厚度小于未超声处理合金，而其数量密度明显高于未超声处理合金，即超声处理能够促进T6态合金中Ω相的形核和析出。热处理工艺、预变形以及主合金元素质量分数对Ω相的析出行为影响较大[11-15]。在本研究中，超声处理造成的元素分布差异使得Ω相析出行为不同。在时效初期，Mg、Ag原子偏聚形成Mg-Ag团簇，继续时效，这些团簇通过结合Cu原子形成Ω相的先驱体[4]，即Mg和Ag确保Ω相的形核率，而Cu则保证了其连续生长。可见，基体中Mg和Ag质量分数的增大有利于Ω相先驱体形成，从而加快Ω相析出。但表4中超声处理合金基体中Mg质量分数与未超声处理合金接近，这是由于Mg在基体中的扩散速率较高。所以更高密度Ω相析出主要归因于超声处理提高了基体中Cu、Ag质量分数以及促使Cu的分布更加均匀，即Ag提高了Ω相形核，而Cu质量分数的升高及均匀分布促使高密度Ω相在晶内均匀大量析出。因此，超声处理对强化相析出行为的影响主要体现在基体中溶质元素质量分数及其分布状态的改变。
3.2　超声处理对硬度的影响
表2结果证实超声处理能有效提高铸态和T6态合金的硬度。而实验合金常见的强化机制为细晶强化、析出强化、固溶强化和位错强化。由于未观察到明显的位错，位错强化对强度的贡献可以忽略不计。Tiryakioglu[16]证明硬度和屈服强度之间存在下列关系：
式中：σs为屈服强度；βa为常数，约为0.303；g为重力加速度，9.8 m/s2；Hv为合金硬度；βb为经验值。将实验所得硬度值代入式（1）中可知，相对UT-0合金，铸态UT-90合金和UT-180合金屈服强度增量分别为35.7 MPa和31.5 MPa，T6态UT-90合金和UT-180合金屈服强度增量分别为29.4 MPa和26.4 MPa。
细晶强化对强度的贡献值σgb遵循Hall-Petch关系[17]：
式中：σ0为常数，取值为10 MPa；k为Hall-Petch系数，取值范围为0.1～0.2 MPa/m0.5，本文取0.1 MPa/m0.5；d为合金的平均晶粒尺寸[17]。
将表5数据代入式（2）中可得，细晶强化对铸态UT-0、UT-90和UT-180合金硬化效果的贡献值分别为18.1 MPa，18.2 MPa和18.3 MPa。可见，超声处理导致的晶粒细化对铸态合金硬度无影响，因此，固溶强化是导致超声处理合金硬度提高的主要原因。对于铸态合金而言，未溶相数量越少、基体内溶质原子分数越高，其强度和硬度越高[6]。从SEM能谱分析结果可知，超声处理后的铸态合金未溶相数量明显降低，基体中Cu和Ag质量分数明显增高，显然过量的Cu和Ag在基体内引起了更大的固溶强化效应，从而使得超声处理后铸态合金的硬度更高。
实验合金作为可热处理强化的合金，细晶强化和固溶强化对其T6态强度的贡献较小，对该状态强度贡献最大的是析出强化，且析出相尺寸越小，析出相数量越多，对合金强度的贡献越大[18]。从图4和表6可知，超声处理后UT-90和UT-180合金中Ω相的数量密度要显著高于UT-0合金，其体积分数也必然超过UT-0合金，这种差异同样源于超声处理对Cu元素均匀分布的促进作用。只有更均匀的Cu元素分布，才能确保时效时合金中不同位置Ω相的同步形核析出，从而引起更高的析出强化效应，提高T6态合金硬度。
4　结论
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1）超声处理降低了铸态合金的枝晶偏析，显著减少第二相的数量，并细化了铸态合金的晶粒尺寸。
2）超声处理增大了基体中Cu、Ag元素的质量分数，导致更高的固溶强化效应，提高了铸态合金的硬度。
3）超声处理提高了时效过程所析出Ω相的数量密度，提升了T6态合金的硬度。
基金
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  • 国家自然科学基金面上项目(52071341)
  • 湖南省自然科学基金青年项目(2020JJ5711)
文献
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2024年第44卷第6期
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doi: 10.3969/j.issn.0253-6099.2024.06.030
  • 接收时间：2024-06-25
  • 首发时间：2026-03-19
  • 出版时间：2024-12-01
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  • 收稿日期：2024-06-25
基金
国家自然科学基金面上项目(52071341)
湖南省自然科学基金青年项目(2020JJ5711)
作者信息
    中南大学　材料科学与工程学院，湖南　长沙　410083

通讯作者:

柏松（1984—），男，江苏盐城人，副教授，主要从事铝合金组织调控与强韧化研究。E-mail：
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2种不同金属材料的力学参数
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species		 占总种数比例
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total species (%)		 属
Genus		 种数
Number of
species		 占总种数比例
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鹅膏菌科Amanitaceae 2 11 5.26 鹅膏菌属 Amanita 10 4.78
小菇科 Mycenaceae 2 12 5.74 丝盖伞属 Inocybe 5 2.39
多孔菌科 Polyporaceae 8 14 6.70 蜡蘑属 Laccaria 5 2.39
红菇科 Russulaceae 3 23 11.00 小皮伞属 Marasmius 6 2.87
小菇属 Mycena 11 5.26
光柄菇属 Pluteus 5 2.39
红菇属 Russula 17 8.13
栓菌属 Trametes 5 2.39
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